Alloy SFE Driver
Zn alloy (SFE 7 mJ m(-2)). The no Cu (23 nm) and no Cu alloy (22 nm) were synthesized using in situ consolidation during cryo and room temperature milling. Stacking fault energy of aluminum alloys was correlated with the . The SFE of the Al-Cr alloy is a little bit above the SFE of pure Al, as in the. Metallic Alloys I know that by decreasing SFE makes decreasing climb phenomena. but I don't know the mechanism. do you help me? up to know the all of the.
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Alloy SFE Driver
In contrast to the CG specimen, the strain-hardening rate is much higher for the MG specimen, Alloy SFE shown in Fig.
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This is because, for the MG specimen, the densities of dislocations and SFs are higher at the early stage of tensile straining in contrast to the CG specimen, as exhibited in Fig. In addition, deformation twins were also recognized when the strain approached to 0. Overall, the higher densities of dislocations and SFs and the early onset of deformation twinning are responsible for the higher strain-hardening rate for the MG specimen in comparison with the CG specimen. When the strain Alloy SFE larger than 0.
Note that if the strain-hardening curve of the FG specimen was shifted to the higher strain region in Fig. This is possibly because the deformation mechanisms are originated mainly from SFs and deformation twinning in the Alloy SFE stages of strain-hardening for the three specimens.
Thus TB can impede the dislocation movement efficiently, inducing a significant increase in strength. For example, Meyers et al.
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- Stacking-fault energy - Wikipedia
In each case, the experimentally observed Hall—Petch slope for twinning is higher than that for the dislocation slip Alloy SFE a result, for those materials with low SFE where deformation twinning involves, there is always a higher strain-hardening rate. For example, in CG FeMn In the present study, a plateau region in the MG specimen and an increased strain-hardening stage in the CG specimen appeared but different deformation patterns were obtained concerning the role of deformation twinning during tensile test.
For the FG specimen, deformation Alloy SFE were observed when the tensile strain is only 0. For the MG specimen, deformation twins did not appear until the strain approached Alloy SFE 0. This indicates that the plateau stage B may be not induced by deformation twins.
Similarly, for the CG specimen, deformation twins did not appear until the strain of 0. Previous study indicates that dislocation glide dominates the deformation of pure Cu during Alloy SFE test at room temperature, and the strain-hardening rate decreases monotonously with increasing the strain irrespective of the grain size Concerning the large number of SFs besides dislocations, they may play a key role in inducing the plateau region B in the MG specimen and the region B in the CG specimen where strain-hardening rate increases with strain. Recent theoretical studies by molecular dynamics simulation reveal the interaction between dislocations and SFs, and it is found that in most cases SFs prevent the glide of other dislocations Alloy SFE slip planes crossing the SF plane 33 This supports the present experimental fact that SFs play an important role in enhancing strain hardening, leading to the plateau region of the MG specimen and the increased strain-hardening region in the CG specimen.
Overall, the present results have clearly provided a new deformation mechanism in low-SFE materials during tensile test.
For the CuAl alloy, deformation twinning indeed plays an important role in sustaining the plasticity but only at the later stage during the tensile test. In contrast, SFs appear just after yielding and they are increasingly activated with increasing the tensile strain until fracture, indicating that SFs may be even more crucial in sustaining the ductility in the Alloy SFE alloy with low SFE. Strain-hardening behaviors of materials with different SFEs In the material with a high SFE, dynamic recovery is favored due to the dislocation cross slip under the quasi-static straining process 11 In that case, the strain-hardening rate is monotonously decreased with increasing the strain In contrast, the strain-hardening behavior is sensitive to the grain size in the material with a low SFE due to the intervening of SFs and deformation twins, as delineated above.
In the stage A, dislocations dominate the plastic deformation during the straining process though SFs also appear, thus the strain-hardening rate decreases sharply in this stage, which is similar to the material with a high SFE. Further increase in strain will activate more SFs and dislocations, which will affect the strain-hardening rate significantly. It is noteworthy that in the CG alloy, there is a stage B where the increase Alloy SFE strength is accelerated with Alloy SFE the strain in the form of an enhancement of strain-hardening rate. In the previous study, it has been considered that this stage is induced by the activity of deformation twinning, and this phenomenon is frequently observed in high-Mn TWIP steels However, SFs instead of deformation twins were detected in this stage.
It is thus concluded that both SFs and deformation twins can induce the increase of strain hardening rate.
Though both Cu-Al alloy and FeMn Figure 5: Schematic illustration on the typical strain-hardening curves of the Alloy SFE FCC materials with high and low SFEs. Deformation patterns of dislocations, stacking faults and deformation twins were inserted at different stages.